Note: Descriptions are shown in the official language in which they were submitted.
70 1 4-~`llB
10893~7
BACKGROUND OF THE INVENTION
Commercially useful copper base alloys whlch possess
a combinatlon of high strength and high electrical
conductivity are usually difficult to obtain because the
methods and elements utilizèd to provide good strength
properties, for example, usually do so at the detriment of
the electrical conductivity of the alloys. From a number
of approaches to the solution of thls problem, two methods
~ o~ achieving the combination o~ high strength and hi~h
; 10 electrical conductivity have been most readily utilized.
The first method is determining and ad~usting the elements
to be alloyed with the base copper to provide inherent
high strength and electrical conductivity properties in the
resulting alloy system. Elements such as zirconium and
chromium have been used in the past as additions to copper
base alloys to provide the desirable strength-conductivity
combination. Precipitation hardened alloys which contain
chromium generally have lower electrical conductlvity
but higher strength than pure copper. The precipitation
o~ zirconium in copper is known to give large increases in
electrical conductivity to the base copper but only small
increases in strength properties over the values for the
solid solution o~ zirconium in copper.
Another method which has been utilized to provlde the
strength-conductivity comblnation ln copper base alloys
includes ad~u9ting the homogenizatlon, hot working,
anneallng and aging o~ the alloy to provLde high strength
properties to the alloy system without reducing the
electrical conductivlty o~ the system. An example of this
approach may be ~ound in U.S. Patent No. 3,930,894,
~1
701 4-Ms
10t~933'7
issued January 6, 1976. mis patent teaches a method of
working phosphor-bronze copper alloys which includes a
high temperature homogenization, hot and cold working,
intermediate annealing and a final heat treatment to
provide desired properties. The alloy system utilized in
said patent may include chromium. This patent does not
discuss treating precipitation hardenable copper base
alloys which contain chromium as an alloylng element.
me present invention is an attempt to overcome the
shortcomings of the alloying elemeni methods and processing
method descrlbed above by treating chromium-containin~
precipitation hardenable copper base alloys so that not
only the strength properties of said alloys are increaqed
after treatment but the electrical conductivity properties
are also increased.
Accordingly, it is a principal ob~ect of the present
invention to provide a method of processing chromium- ~
containing precipitation hardenable copper base alloys in -
such a manner so as to increase both the strength and
electrical conductivity properties of the alloys.
Further ob~ects and advantages o~ the present
lnvention will become apparent ~rom a consideratlon o~ the
~ollowing ~peclficatlon.
SUMMARY OF THE INVENTION
~i In accordance with the present lnvention it has been
~ound that the foregoing ob~ect may be readily achieved by
processing a precipitation hardenable chromlum-containlng
copper base alloy according to the following steps:
~a) casting a precipitation hardenable copper base
alloy which contalns chromium,
-2-
.
7014-M3
10 8~3 ~
(bl) hot working the alloy at a starting temperature
of 850-950C; or
tb2) hot working the alloy at a starting temperature
of 950-1000C to ef~ect the maximum solid
solution of all alloying elements;
(c) if step tbl~ has been ~tilized, solution annealing
the worked alloy at a solutionizing temperature
of 950-1000C, preferably 975-1000C, for a
period of time sufficient to insure the maximum
solid solution of all alloying ele~ents;
~d~ rapidly cooling said alloy to maintain said
maximum solid solution of all alloying elements;
~e~ cold working the alloy to a total reduction o~
at least 60% and preferably to at least 75%;
tf~ aging said alloy at 400-500C ~or one to 24 hours
and preferably 430-470C for 2 to 10 hours;
~g~ cold working the alloy to a total reduction of
at least 50% and preferably to at least 75%;
~h-~ aging said alloy at 150-250C for one to 24
hours and preferably 175-225C for 2 to 10 hours;
and
~i) optionally cold working said alloy to the final
de~ired temper.
DETAILED D-ESC~IPTION
The present invention provldes an lmprovement in the
combinatlon o~ strength ar.d electrical conducti~ity
properties of the alloy system being processed through the
steps o~ solution annealing to bring all alloying elements
into maximum solid solution, cold working the alloy to
such a degree so as to strain harden the alloy to high
:: ' ' '
7014-MB
10~933~
strength and f~nally sub~ecting the alloy to an aging/cold
working combination o~ steps.
The alloy system which may be processed effectively
according to`the present invention must be precipitation
hardenable and should contain at least a small percentage
of chromium. Addltional alloying elements may be added -
to the copper-chromium system, among which are zirconium,
vanadium and nlobium. Other elements may also be added to
achleve particularly desirable strength and/or conductivity
properties.
The hot working step of the processing of the oresent
invention may by itself be used to provlde the effect of
solution annealing. This is generally accomplished by -
performing the hot working at a temperature which is high
enough to place all of the alloylng elements into maximum
solid solution. This temperature should be at least 950C
with a preferred temperature range of 975-1000C to insure
said maximum solid solution.
The alloys utilized in said process are generally
cast at a temperature which ranges between 25C above the
melting polnt of the alloy up to approximately 1300C.
Thls casting may be performed by any known and convenient
method.
The hot working reductlon requlrement is generally
what is mo~t convenient for ~urther working. The process
utilized ln the present inventlon has no partlcular
dimensional requirements other than that the hot working
be accompli2hed according to good mill practice. If the
hot working step is also utilized to provide the solution
annealing of the alloy, the main consideration is that the
7014-MB
lQ 89 ~
hot working be per~ormed to e~fect the maximum solid
solution of all the alloying elements, This permits the
later precipitation during aging of the most desirable
hlgh volume fraction of fine uniform dispersions of
lntermediate solid phases consisting o~ chrom~um, zirconium
and niobium, the phases existing in the alloy matrix either
as dependent or intermixed phases. The solution annealing
step of the process utilized in the present invention,
whether performed as part of the hot working step or as a
separate step after hot working, also pro~ldes ~or the
maximum solid solution of all the alloying elements. This
solution annealing is accomplished at a temperature between
950 and 1000C. It is preferred that the solution
annealing be accomplished at a temperature between 975 and
1000C. It should be noted that this solution annealing
step can take place at any point in the instant process
a~ter the initial hot working step, provided that rapid
cooling, cold working and aging steps are performed a~ter
the solution annealing step.
The alloy, after being either hot worked alone or
hot worked in combination with a separate solution
annealing step, is then rapidly cooled so as to maintain
the maximum solld solution of all alloying elements.
Cooling to 350C or less is necessary to malntain said
maximum solid solution. Thls cooling may be accomplished
accordin~ to procedures well known in this art, using
either air or a llquld as the cooling medium.
The next step in the process utilized in the present
; invention is cold working of the alloy. Thls cold wor~ing
~ 30 step is utilized to provide an increase in strength to the
70l4-rTs
- 10893;~7
alloy as well as being used to meet dimensional require-
ments. The alloy is generally cold worked to an initial
reduction of at least 60% and preferably at least 75%.
This relatively high cold reduction serves to impart more
strain hardening to the alloy prior to aging as well 2S
impart improvement in the electrical conductivity of the
aged alloy. The improvement in electrical conductivity
after aging of the alloy is presumably brought about by -
altering the kinetics of precipitation in the alloy matrix.
Thls cold working step may be the final cold working before
aglng of the alloy if the alloy is reduced to the final
desired dimensions. The cold working may be utilized in
cycles with the aging so that a cycle may end with either
an aging step or a cold working step.
The cold worklng of the alloy is followed by an aglng
step. Thls aglng ls generally performed at a temperature
between 400-500C for one to 24 hours, preferably between
430-470C for 2 to 10 hours. This aging is performed to
lncrease the mechanlcal and electrical conductivity
2~ properties of the alloy. After this aglng step, the alloy
is further cold worked to a total reduction of at least
50% and preferably 75%. The alloy is then aged at a
temperature between 150-250C for one to 24 hours, prefer-
ably between 175-225C for 2 to 10 hours. This final aglng
ls performed to restore the electrical conductivlty values
to the highly cold worked alloy and thus provide the
deslrable comblnation of high electrlcal conductlvity and
hlgh strength ln the alloy.
The process of the present lnvention also contempla~es
the steps of fabricating a f~nal deslred article out of the
--6--
7014-M3
10 ~ 3 ~ ~
worked alloy material and then sub~ecting said ~abricated
article to the low temperature thermal treatment of the
present invention. In other words, the~inal cold working
step before the final low temperature thermal treatment
step o~ the present invention will become a fabricating
cold working step.
The process o~ the present invention and the
advantages obtained thereby may be more readily unders~ood
from a consideration of the ~ollowing illustrative example.
EXAMPLE
An alloy having a composition of 0.60% by weight -
chromium, 0.16% by welght zirconium, 0.18~ by weight
niobium, balance essentially copper was vacuum melted and
cast under an argon protective atmosphere. After hot
; working the alloy, it was solution annealed at 1000C for
45 minutes to place all alloying elemènts lnto maximum
solid solution. The alloy was then cooled and sub~ected to
cold working with a 75% reduction. The alloy was sub~ected
to heat treatment of 450C ~or 4 hours and was then cold
2G worked to an additional 75% reduction. Properties Of the
alloy were measured at this point in the proce~sing and
agaln after an additional heat treatment at 200C ~or 8
hours. Both the strength and electrical conductivity
properties of the alloy increased after the additional 1QW
temperature heat treatment. These results are shown in
Table I. For a comparison, this processing was compared to
another processing system from the literature. This other
s~stem contained an alloy composed o~ copper with 0.40% by
weight chromium, 0.15% by weight zirconium, 0.05% by weight
magnesium~ balance essentially copper. This alloy was
' 0l4-r~s
lQ~3~
sub~ected to the processing shown in Table I and measure-
ments o~ its properties were taken both after cold reduction
and a~ter an additional heat treatment.
TABLE I
ELEC~CAL CONDU~ AND STRENGIH COMPARISOM PR0PERTI~X
Processing UIS ~Ksi) 0.2% YS (ksi) % IACS
S.A. + 75% CR + 450C/4 hrs. + 92 88 71
75% CR ~A)
(A) + 200C/8 hrs. 98 93 74
Literature Processing (1)
S.A. + 60% RA + 450C/1/2 hr. + 100 97 65
90% RA (A)
(A) + 450C/1/2 hr. 95 90 80
(1) P. W. Taubenblatt et al., Metals E~neering ~ rterly,
November 1972, Volume 12, p. 1.
Table I illustrates the improvement in both strength
and electrical conductivity obtained by the final low
temperature thermal treatment in the process of the
present invention. This improvement in both strength and
conductivity properties is to be contrasted with the
properties obtained from the high temperature thermal
treatment from the llterature processing, where the
strength properties were diminished with treatment and
only the electrical conductivity wa~ improved. The
process o~ the present invention therefore presents an
opportunity to improve both the strength and electrical
conductlvity properties of an alloy without detrimentally
affecting either one o~ the properties.
3o
